JPH05306453A - Production of high-strength plated steel wire - Google Patents
Production of high-strength plated steel wireInfo
- Publication number
- JPH05306453A JPH05306453A JP13781492A JP13781492A JPH05306453A JP H05306453 A JPH05306453 A JP H05306453A JP 13781492 A JP13781492 A JP 13781492A JP 13781492 A JP13781492 A JP 13781492A JP H05306453 A JPH05306453 A JP H05306453A
- Authority
- JP
- Japan
- Prior art keywords
- steel wire
- plating
- bath
- zinc
- wire rod
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Landscapes
- Coating With Molten Metal (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は高強度めっき鋼線材の製
造法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a high strength plated steel wire rod.
【０００２】[0002]
【従来の技術及びその技術的課題】強度部材として使用
される鋼線材たとえば、ＡＣＳＲ用鋼線、電話線用吊り
線、ケーブルなどの支持線、鉄道トロリー線のメッセン
ジャーケーブル、ロープ用素線などにおいては良好な耐
食性が要求される。このような特性を得るためのめっき
法として、従来、溶融亜鉛めっき法が用いられている
が、最近、より高い耐食性の要求に応ずるべく、特開昭
６０−４４５６３号公報などにおいて、亜鉛−アルミニ
ウム合金めっきを鋼線類に施すことが提案されている。
この亜鉛−アルミニウム合金めっきは、亜鉛めっきの２
倍の耐食性を有することから普及しつつあるが、従来の
亜鉛−アルミニウム合金めっきは、先行技術に示されて
いるように、下地めっきとして溶融純亜鉛めっきを施
し、次いで溶融亜鉛−アルミニウム合金めっきを施すい
わゆる二浴めっき法が採用されていた。しかし、溶融亜
鉛めっき法や二浴めっき法の下地用溶融亜鉛めっきにお
いては、めっき浴の温度が亜鉛の溶融点温度(４１９.４
℃)プラス３０℃の４５０℃前後に保持され、この浴に
鋼線材を連続的に浸漬し、引き上げることでめっきが行
われる。この際に鋼線材はめっき浴中に長い時間浸漬さ
れるため、鋼線材はめっき浴の温度にまで上昇する。2. Description of the Related Art Steel wires used as strength members, for example, steel wires for ACSR, suspension wires for telephone lines, support wires for cables, messenger cables for railway trolley wires, strand wires for ropes, etc. Is required to have good corrosion resistance. As a plating method for obtaining such characteristics, a hot dip galvanizing method has hitherto been used, but recently, in order to meet the demand for higher corrosion resistance, JP-A-60-44563 discloses a zinc-aluminum method. It has been proposed to apply alloy plating to steel wires.
This zinc-aluminum alloy plating is equivalent to zinc plating 2
Although it is becoming popular because it has double the corrosion resistance, the conventional zinc-aluminum alloy plating, as shown in the prior art, is subjected to hot-dip pure zinc plating as an undercoat, and then hot-dipped zinc-aluminum alloy plating. The so-called two-bath plating method was used. However, in the hot dip galvanizing method for the undercoat of the hot dip galvanizing method or the two bath plating method, the temperature of the plating bath is the melting point temperature of zinc (419.4).
(° C) plus 30 ° C, which is maintained around 450 ° C, the steel wire rod is continuously dipped in this bath and pulled up to perform plating. At this time, since the steel wire rod is immersed in the plating bath for a long time, the temperature of the steel wire rod rises to the temperature of the plating bath.
【０００３】ここで、製造対象の鋼線が高い引張り強度
を要求されないものである場合は上記処理条件でもあま
り問題はない。しかし、製造対象の鋼線が１８０kgf/mm
2を越えるような高い引張り強度である場合、材料とし
ての高強度鋼線材は、熱処理を施した後、冷間引き抜き
加工によって高強度化されるものであり、この高強度鋼
線材は加熱によって軟化し強度が低下する。図１は直径
3.0mmの冷間引き抜き鋼線を、ソルト浴中で２０秒浸漬
後空中放冷した場合の加熱処理温度と引張り強さの関係
を示しており、３００℃以上ことに４００℃を越える温
度に長く加熱されると強度の低下が著しいことがわか
る。そして前記のように溶融亜鉛めっきは４５０℃前後
まで加熱される結果、高強度鋼線材は軟化が進行し、耐
食性は満足しえても肝心の強度特性が大きく低下するこ
とを避けられなかった。Here, when the steel wire to be manufactured does not require high tensile strength, there is no problem even under the above treatment conditions. However, the steel wire to be manufactured is 180 kgf / mm
If the tensile strength exceeds 2 , the high-strength steel wire rod as a material will be strengthened by cold drawing after heat treatment.This high-strength steel wire rod is softened by heating. Strength decreases. Figure 1 is the diameter
It shows the relationship between the heat treatment temperature and the tensile strength when a 3.0 mm cold drawn steel wire is immersed in a salt bath for 20 seconds and then left to cool in the air. It can be seen that the strength is significantly reduced when heated. As described above, the hot dip galvanization is heated up to around 450 ° C. As a result, the high-strength steel wire material is gradually softened, and it is unavoidable that the core strength characteristics are greatly deteriorated even though the corrosion resistance is satisfied.
【０００４】[0004]
【課題を解決するための手段】本発明は前記のような問
題点を解消しようとするもので、その目的とするところ
は、良好な耐食性と高強度を兼ね備えためっき鋼線材を
能率よく安価に生産する方法を提供することにある。こ
の目的を達成するため本発明は、冷間引き抜き鋼線材に
平均厚みが１０〜１００μmの耐食めっきを施す方法で
あって、鋼線材を前処理後フラックス処理を施し、浴温
度３９５〜４３０℃でアルミニウム４〜６重量％を含む
亜鉛−アルミニウム合金めっき浴中を線速２０〜５０m/
minで通過させて一浴めっきする構成としたものであ
る。SUMMARY OF THE INVENTION The present invention is intended to solve the above-mentioned problems, and an object of the present invention is to efficiently and inexpensively provide a plated steel wire rod having both good corrosion resistance and high strength. It is to provide a method of producing. In order to achieve this object, the present invention is a method of subjecting cold drawn steel wire rods to corrosion-resistant plating having an average thickness of 10 to 100 μm, wherein the steel wire rods are subjected to a flux treatment after pretreatment and at a bath temperature of 395 to 430 ° C. Linear velocity of 20-50 m / in a zinc-aluminum alloy plating bath containing 4-6% by weight of aluminum
It is configured such that one bath plating is performed by passing it at min.
【０００５】以下本発明を添付図面に基いて説明する。
図２は本発明による高強度めっき鋼線材の製造工程を概
略的に示している。めっきする鋼線材ａは、冷間引き抜
き加工された引張り強さ１８０kgf/mm2以上のものであ
り、一般にＪＩＳ規格ＳＷＲＨ８２Ｂで示される硬鋼線
材ゃこれに強化元素を添加したものを原料線材として使
用し、これを鉛パテンティング処理し、冷間伸線加工さ
れたものである。１は鋼線材ａの供給スイフト、２は溶
融鉛浴であり、４００℃前後の温度に保持され、前工程
の伸線潤滑剤などをバーンアウトし、鋼線材表面の脱脂
を行い、次の水冷槽３において冷却する。５は１５〜１
６％濃度の塩酸浴、６は水洗槽であり、鋼線材ａは溶融
鉛浴２による処理で生成した薄い酸化膜などの異物が除
去され、水洗される。The present invention will be described below with reference to the accompanying drawings.
FIG. 2 schematically shows a manufacturing process of the high strength plated steel wire rod according to the present invention. The steel wire a to be plated is cold drawn and has a tensile strength of 180 kgf / mm 2 or more. Generally, a hard steel wire shown in JIS standard SWRH82B or a material obtained by adding a reinforcing element to it is used as a raw material wire. However, this was subjected to lead patenting treatment and cold drawn. Reference numeral 1 is a supply swift of the steel wire rod a, 2 is a molten lead bath, which is maintained at a temperature of around 400 ° C., burns out a wire drawing lubricant and the like in the previous step, degreases the surface of the steel wire rod, and then cools with water. Cool in tank 3. 5 is 15 to 1
A 6% concentration hydrochloric acid bath and 6 are washing tanks, and the steel wire rod a is washed with water after removing foreign matters such as thin oxide film generated by the treatment with the molten lead bath 2.
【０００６】次に鋼線材ａはフラックス槽７を通過する
ことによってフラックス処理が行われる。そして、この
ようにフラックス処理された鋼線材ａは、乾燥炉８を通
過することによってフラックス中の水分が乾燥され、次
いでめっき浴９にシンカーロール１０によって導かれめ
っきされる。ここで、めっき条件は、本発明では次のも
のとする。 めっき金属は、アルミニウムが重量比で４〜６％含む
亜鉛−アルミニウム合金であり、これを使用した一浴め
っきでめっきする。 めっき浴温度は、３９５〜４３０℃とする。 線速を２０〜５０m/minとする。Next, the steel wire rod a is subjected to a flux treatment by passing through the flux tank 7. Then, the flux-treated steel wire a is dried in the flux by passing through the drying furnace 8 and then introduced into the plating bath 9 by the sinker roll 10 to be plated. Here, the plating conditions are as follows in the present invention. The plating metal is a zinc-aluminum alloy containing aluminum in an amount of 4 to 6% by weight, and plating is performed by single bath plating using this alloy. The plating bath temperature is 395 to 430 ° C. The linear velocity is 20 to 50 m / min.
【０００７】フラックス法による一浴めっきで亜鉛−ア
ルミニウム合金めっきを採用することは、溶融亜鉛めっ
きや二浴式による溶融亜鉛下地めっきにおけるようなめ
っき層と鋼素地上にＦｅ−ＺｎあるいはＦｅ−Ａｌ−Ｚ
ｎという金属化合物層をさせない利点がある。そして、
これらの条件を採用することによって、溶融めっ
きにより鋼線の受ける熱履歴温度を低くして強度低下を
抑制し、より高い強度のめっき鋼線とすることができ
る。詳述すると、めっき浴９をアルミニウム濃度が重量
比で４〜６％の範囲にする理由は、この範囲が最もよい
耐食性を示し、かつ、めっき時の溶融金属の流動性を高
くすることができ、さらに、ドロスの発生が少ないため
である。アルミニウム濃度が４％を下回る場合には、耐
食性が低下するため不可である。一方、アルミニウム濃
度が６％を超える場合、溶融金属の流動性が悪くなるた
め、めっき表面が粗くなったり、偏肉が発生しやすくな
る。したがって、上記アルミニウム濃度が必要である。The use of the zinc-aluminum alloy plating in the one-bath plating by the flux method means that Fe-Zn or Fe-Al is formed on the plating layer and the steel substrate as in the hot-dip galvanizing or the double-bath hot dip galvanizing. -Z
There is an advantage that the metal compound layer of n is not formed. And
By adopting these conditions, it is possible to lower the heat history temperature that the steel wire receives by the hot dip coating to suppress the strength reduction and to obtain a plated steel wire having higher strength. More specifically, the reason why the aluminum concentration in the plating bath 9 is in the range of 4 to 6% by weight is that this range exhibits the best corrosion resistance and that the fluidity of the molten metal during plating can be increased. This is also because the dross is less likely to occur. If the aluminum concentration is less than 4%, it is not possible because the corrosion resistance decreases. On the other hand, when the aluminum concentration exceeds 6%, the fluidity of the molten metal deteriorates, so that the plating surface becomes rough and uneven thickness easily occurs. Therefore, the above aluminum concentration is necessary.
【０００８】次に、めっき浴温度と線速は鋼線の加熱に
よる軟化度合いに影響を与える。すなわち、鋼線の加熱
による軟化度合いは、到達温度と加熱保持時間の双方の
影響を受け、到達温度が高いほど、また加熱保持時間が
長いほど軟化は進行する。本発明においては、アルミニ
ウム濃度が重量比で４〜６％のめっき合金としたため、
溶融点温度を亜鉛と比べて約４０℃低くすることができ
る。ただ、めっき浴温度が３９５℃を下回る温度では溶
融金属の流動性が悪いため、めっき外観が不安定とな
り、不可である。上限を４３０℃としたのは、これを上
回る温度では熱履歴温度が高くなり、材料の強度が低下
するからであり、より好ましい温度範囲は、４００〜４
１５℃である。線速は、上記のように鋼素地上にめっき
金属との金属間化合物層の生成がなく、また前記アルミ
ニウム濃度範囲から浴の流動性が高いため早くすること
ができるが、一方、めっき付着量１０〜１００μｍ(７
０〜７００ｇ／ｍ2）の制御とも関連する。２０m/min未
満では加熱保持時間が長くなるとともに、めっきが薄く
なり過ぎて所望される耐食性が発揮されない。５０m/mi
nを超える線速では、加熱保持時間は短くてすむが、必
要とされるめっき厚み以上となる。したがって、２０〜
５０m/minであり、これを在めっき浴時間でいえば、１
０秒前後である。Next, the plating bath temperature and the linear velocity affect the degree of softening of the steel wire due to heating. That is, the degree of softening of the steel wire due to heating is affected by both the ultimate temperature and the heating and holding time, and the higher the ultimate temperature and the longer the heating and holding time, the more the softening progresses. In the present invention, since the aluminum alloy has a plating ratio of 4 to 6% by weight,
The melting point temperature can be lowered by about 40 ° C. as compared with zinc. However, when the temperature of the plating bath is lower than 395 ° C., the fluidity of the molten metal is poor, and the plating appearance becomes unstable, which is not possible. The upper limit is set to 430 ° C., because the heat history temperature increases and the strength of the material decreases at a temperature above this, and a more preferable temperature range is 400 to 4
It is 15 ° C. The linear velocity can be increased because there is no formation of an intermetallic compound layer with the plating metal on the steel substrate as described above, and the fluidity of the bath is high from the aluminum concentration range. 10 to 100 μm (7
It is also related to the control of 0 to 700 g / m 2 . If it is less than 20 m / min, the heating and holding time becomes long, and the plating becomes too thin so that the desired corrosion resistance is not exhibited. 50m / mi
At a linear velocity exceeding n, the heating and holding time can be short, but the required plating thickness or more. Therefore, 20 to
50m / min, which is 1 in terms of plating bath time
It is around 0 seconds.
【０００９】上記のように、溶融亜鉛−アルミニウム合
金めっきの付着された鋼線材ａはシンカーロール１０を
経て上方に導かれ、合金めっき浴上に設けられている絞
り部１１で付着量が調整されたのち、冷却装置１２によ
って合金めっきが凝固冷却される。溶融めっきの絞り
は、木炭、アスベスト、あるいはガスグラベルなどの固
体絞りでもよいが、不めっきやめっき厚みの不均一(偏
肉)を回避し、めっき厚みが大きくなった部分の疲労特
性が劣化するのを防止する点からは、非酸化性ガスで絞
りを行うことが好ましい。図示のものでは、絞り部１１
は、下部開口をめっき浴９に浸漬させた筒状のシールボ
ックス１１０からなり、頂部には鋼線材ａの通過を許す
導孔１１１が設けられ、側部には図示しない供給源から
導かれた非酸化性ガスたとえば、窒素ガス、アルゴンガ
ス、プロパンガス、アンモニア分解ガスなどの導入部１
１２が接続されている。シールボックス１１０内は外気
と遮断され、内部に導入部１１２から供給された非酸化
性ガスが充満し、一部が導孔１１１から流出することで
鋼線材ａに付着した溶融亜鉛−アルミニウム合金めっき
が絞られる。この場合、めっき付着量は非酸化性ガスに
よっても制御される。一般に非酸化性ガスの流量は、通
線する線条材１本当り３〜７ｌ／minことに付着量レベ
ルの安定する４〜５ｌ／minが適している。３ｌ／min未
満の場合は、シールドボックス中の雰囲気を非酸化性に
保てないし、７ｌ／minをこえる流量は不経済である。As described above, the steel wire rod a to which the hot dip zinc-aluminum alloy plating is adhered is guided upward through the sinker roll 10 and the adhesion amount is adjusted by the narrowing portion 11 provided on the alloy plating bath. After that, the alloy plating is solidified and cooled by the cooling device 12. The squeeze for hot dip coating may be solid squeeze such as charcoal, asbestos, or gas gravel, but avoids non-plating and uneven plating thickness (uneven thickness) and deteriorates the fatigue characteristics of the thickened part. From the viewpoint of preventing the above, it is preferable to perform throttling with a non-oxidizing gas. In the illustrated example, the throttle unit 11
Consists of a cylindrical seal box 110 whose lower opening is immersed in the plating bath 9, a guide hole 111 is provided at the top to allow passage of the steel wire a, and a side is led from a supply source (not shown). Introducing section 1 for non-oxidizing gas such as nitrogen gas, argon gas, propane gas, and ammonia decomposition gas
12 are connected. The inside of the seal box 110 is shielded from the outside air, the inside is filled with the non-oxidizing gas supplied from the introduction part 112, and a part of the non-oxidizing gas flows out from the guide hole 111, so that the molten zinc-aluminum alloy plating adhered to the steel wire rod a. Is narrowed down. In this case, the coating weight is also controlled by the non-oxidizing gas. Generally, the flow rate of the non-oxidizing gas is suitable to be 3 to 7 l / min for each wire material that runs through, and 4 to 5 l / min where the deposition amount level is stable. If it is less than 3 l / min, the atmosphere in the shield box cannot be kept non-oxidizing, and a flow rate exceeding 7 l / min is uneconomical.
【００１０】実施例１ 次に本発明の実施例を示す。ＪＩＳ硬鋼線材ＳＷＲＨ８
２Ｂ(C:０．８３wt％、Mn:０．７１wt％を含む)、６.５
mmφに鉛パテンティング処理を施した後、冷間伸線加工
を行って、直径２.５３mm、引張り強さ２０８kgf/mm2の
裸鋼線を製作し、これをめっき用の原線として、溶融亜
鉛めっき法(A)、第一浴として亜鉛めっきを行い第二浴
として亜鉛−アルミニウム合金めっきを行う二浴法
(B)、および一浴法の本発明法(E)(F)と比較法(C)(D)に
よってめっき処理した。めっきはいずれも付着量２６０
g/m2を狙って行った。このめっきは図２に示す工程で実
施した。いずれも、原線は前処理として、４００℃の溶
融鉛浴での脱脂、濃度１５％の塩酸による酸洗後、水洗
され、さらにフラックス処理を行い、熱風乾燥炉で乾燥
後、めっき浴に浸漬し、引き上げた。めっき浴の組成
は、(B)〜(F)の亜鉛−アルミニウム合金めっき浴のＡｌ
濃度はすべて４．６wt％とした。続いて、ガス式絞り部
を使用し、窒素ガス、鋼線１本当り５ｌ／minの条件で
めっき付着量を制御し、水冷ノズルを使用して水冷水４
５℃により凝固冷却させた。この結果を表１に示す。な
お、耐食性はＪＩＳ Ｚ ２３７１の塩水噴霧試験によ
り赤錆発生までの時間を測定したデータである。なお、
延性、靭性はいずれのものも問題なかった。Example 1 Next, an example of the present invention will be described. JIS hard steel wire rod SWRH8
2B (including C: 0.83 wt% and Mn: 0.71 wt%), 6.5
After subjecting mmφ to lead patenting, cold drawing is performed to produce bare steel wire with a diameter of 2.53 mm and a tensile strength of 208 kgf / mm 2 , which is melted as the original wire for plating. Zinc plating method (A), two-bath method in which zinc plating is performed as the first bath and zinc-aluminum alloy plating is performed as the second bath
(B), and the one-bath method of the present invention (E) (F) and the comparative method (C) (D). The amount of plating is 260
I aimed at g / m 2 . This plating was performed in the process shown in FIG. In both cases, as the pretreatment, the original wire was degreased in a molten lead bath at 400 ° C, pickled with hydrochloric acid having a concentration of 15%, washed with water, further subjected to flux treatment, dried in a hot air drying oven, and then immersed in a plating bath. Then raised. The composition of the plating bath is (B) to (F) zinc-aluminum alloy plating bath Al
All the concentrations were 4.6 wt%. Then, using a gas-type throttle part, the amount of plating adhered was controlled under the conditions of nitrogen gas and 5 l / min per steel wire, and water-cooled water was used to control water-cooled water 4
It was solidified and cooled by 5 ° C. The results are shown in Table 1. The corrosion resistance is data obtained by measuring the time until the occurrence of red rust by the salt spray test of JIS Z2371. In addition,
There was no problem in ductility and toughness.
【００１１】[0011]
【表１】 [Table 1]
【００１２】この表１から本発明のめっき条件を採用す
ることによって、引張り強さのすぐれためっき鋼線が得
られることがわかる。It can be seen from Table 1 that by applying the plating conditions of the present invention, a plated steel wire having excellent tensile strength can be obtained.
【００１３】実施例２ 実施例１のＪＩＳ硬鋼線材ＳＷＲＨ８２Ｂにおいて、Si
成分量のみを0.9%にした７.０mmφの線材に鉛パテンテ
ィング処理を施した後、冷間伸線加工を行って、直径
２.４３mm、引張り強さ２３０kgf/mm2の裸鋼線を製作
し、これをめっき用の原線として３種のめっき法でめっ
きした。(G)は溶融亜鉛めっき法、(H)は二浴法、(I)は
本発明法である。(H)のめっき浴と(I)のめっき浴は、ア
ルミニウム濃度を４．６％とした。この結果を表２に示
す。Example 2 In the JIS hard steel wire rod SWRH82B of Example 1, Si
After subjecting a 7.0 mmφ wire rod containing only 0.9% of the component amount to lead patenting treatment, cold drawing is performed to produce a bare steel wire with a diameter of 2.43 mm and a tensile strength of 230 kgf / mm 2. Then, this was used as the original wire for plating and plated by three kinds of plating methods. (G) is the hot dip galvanizing method, (H) is the two-bath method, and (I) is the method of the present invention. In the plating bath of (H) and the plating bath of (I), the aluminum concentration was 4.6%. The results are shown in Table 2.
【００１４】[0014]
【表２】 [Table 2]
【００１５】表２から明らかなように、本発明によれば
亜鉛めっき法に比較して約５％も高い引張り強さのめっ
き鋼線が得られることがわかる。この結果、同一強度の
鋼線を得るのに約５％の断面積の減少化が可能であり、
それによって各用途での軽量化を図ることができる。As is clear from Table 2, according to the present invention, a plated steel wire having a tensile strength as high as about 5% as compared with the galvanizing method can be obtained. As a result, it is possible to reduce the cross-sectional area by about 5% to obtain a steel wire of the same strength.
As a result, the weight of each application can be reduced.
【００１６】[0016]
【発明の効果】以上説明した本発明の請求項１と２によ
るときには、良好な耐食性と高い強度を持つめっき鋼線
を製造することができ、しかも、線速が早いため生産性
がよく、設備的にも二浴法に比べて安価ですむというす
ぐれた効果が得られる。According to the first and second aspects of the present invention described above, a plated steel wire having good corrosion resistance and high strength can be produced, and since the wire speed is fast, the productivity is good and the equipment is good. The superior effect is that it is cheaper than the double bath method.
【図１】冷間引き抜き鋼線の加熱処理後の引張り強さの
変化を示す線図である。FIG. 1 is a diagram showing changes in tensile strength of a cold drawn steel wire after heat treatment.
【図２】本発明による亜鉛−アルミニウム合金めっき鋼
線材のめっき法の工程の一例を示す説明図である。FIG. 2 is an explanatory view showing an example of a process of a plating method of a zinc-aluminum alloy plated steel wire according to the present invention.
７ フラックス槽 ９ めっき浴 １１ 絞り部 7 Flux tank 9 Plating bath 11 Drawing part
Claims (2)
００μmの耐食めっきを施す方法であって、鋼線材を前
処理後フラックス処理を施し、浴温度３９５〜４３０
℃、アルミニウム４〜６重量％を含む亜鉛−アルミニウ
ム合金めっき浴中を線速２０〜５０m/minで通過させて
一浴めっきすることを特徴とする高強度めっき鋼線材の
製造法。1. A cold drawn steel wire rod having an average thickness of 10 to 1
It is a method of applying corrosion-resistant plating of 00 μm, in which a steel wire is pretreated and then fluxed, and a bath temperature is 395 to 430.
A method for producing a high-strength plated steel wire rod, which comprises passing a zinc-aluminum alloy plating bath containing aluminum at 4 to 6% by weight at a linear velocity of 20 to 50 m / min for single bath plating.
００〜４１５℃である請求項１に記載の高強度めっき鋼
線材の製造法。2. The zinc-aluminum alloy plating bath temperature is 4
The method for producing a high-strength plated steel wire rod according to claim 1, wherein the temperature is from 00 to 415 ° C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13781492A JPH05306453A (en) | 1992-04-30 | 1992-04-30 | Production of high-strength plated steel wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13781492A JPH05306453A (en) | 1992-04-30 | 1992-04-30 | Production of high-strength plated steel wire |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05306453A true JPH05306453A (en) | 1993-11-19 |
Family
ID=15207483
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13781492A Pending JPH05306453A (en) | 1992-04-30 | 1992-04-30 | Production of high-strength plated steel wire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05306453A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101102950B1 (en) * | 2008-10-21 | 2012-01-09 | 안병준 | Plating method of plated wire having uniform thickness |
| WO2014022041A1 (en) * | 2012-08-01 | 2014-02-06 | Baker Hughes Incorporated | Corrosion-resistant resilient member |
| EP3680507A1 (en) * | 2019-01-11 | 2020-07-15 | NV Bekaert SA | Method for making a spring |
-
1992
- 1992-04-30 JP JP13781492A patent/JPH05306453A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101102950B1 (en) * | 2008-10-21 | 2012-01-09 | 안병준 | Plating method of plated wire having uniform thickness |
| WO2014022041A1 (en) * | 2012-08-01 | 2014-02-06 | Baker Hughes Incorporated | Corrosion-resistant resilient member |
| EP3680507A1 (en) * | 2019-01-11 | 2020-07-15 | NV Bekaert SA | Method for making a spring |
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